Magnetic nanoprecipitates and interfacial spin disorder in zero-field-annealed Ni50Mn45In5 Heusler alloys as seen by magnetic small-angle neutron scattering

Magnetic-field-dependent small-angle neutron scattering is employed to disclose the zero-field annealing-induced spin disorder around magnetic nanoprecipitates in an off-stoichiometric Ni50Mn45In5 Heusler alloy.

Shell ferromagnetism is a new functional property of certain off-stoichiometric Ni-Mn-In Heusler alloys, with a potential application in non-volatile magnetic memories and recording media. One key challenge in this field remains the determination of the structural and magnetic properties of the nanoprecipitates that are the result of an annealing-induced segregation process. Thanks to its unique mesoscopic length scale sensitivity, magnetic small-angle neutron scattering appears to be a powerful technique to disclose the microstructure of such annealing-induced nanoprecipitates. In this study, the microstructure of a zero-field-annealed off-stoichiometric Ni 50 Mn 45 In 5 Heusler alloy is investigated by unpolarized magnetic small-angle neutron scattering. The neutron data analysis reveals a significant spin-misalignment scattering, which is mainly related to the formation of annealing-induced ferromagnetic nanoprecipitates in an antiferromagnetic matrix. These particles represent a source of perturbation which, due to dipolar stray fields, gives rise to canted spin moments in the surroundings of the particle-matrix interface. The presence of anticorrelations in the computed magnetic correlation function reflects the spatial perturbation of the magnetization vector around the nanoprecipitates. The magnetic field dependence of the zero crossing and the minima of the magnetic correlation function are qualitatively explained using the law of approach to ferromagnetic saturation for inhomogeneous spin states. More specifically, at remanence, the nanoprecipitates act magnetically as one superdefect with a correlation length that lies outside the experimental q range, whereas near saturation the magnetization distribution follows each individual nanoprecipitate. Analysis of the neutron data yields an estimated size of 30 nm for the spin-canted region and a value of about 75 nm for the magnetic core of the individual nanoprecipitates.

Introduction
Over the past few decades off-stoichiometric bulk Ni 50 Mn 50Àx -In x Heusler alloys have raised a lot of interest because of their multifunctional properties. Among the most well known and best studied properties are the magnetocaloric effect (Liu et al., 2012), magnetic shape-memory effects (Umetsu et al., 2009), the giant Hall effect , large magnetoresistance (Yu et al., 2006;Sharma et al., 2006) and exchange bias effects Wang et al., 2011). These phenomena originate from the structural and magnetic phase transition that lies in a narrow composition range between a high-temperature cubic austenite phase with long-range ferromagnetic (FM) correlations and a low-temperature modulated/nonmodulated tetragonal martensite phase with short-range frustrated antiferromagnetic (AF) correlations (Krenke et al., 2006;Ito et al., 2007).
More recently, a new functionality, termed shell ferromagnetism, was discovered in the martensitic Heusler Ni 50 Mn 45 In 5 alloy (Ç akır et al., 2016), and later on extended to all off-stoichiometric Ni 50 Mn 50Àx In x alloys with x up to 25 at.% (Ç akır et al., 2017). When annealed at high temperatures (650-750 K) and under a magnetic field (of up to 9 T), the compound segregates into predominantly cubic FM nanosized (Heusler) Ni 50 Mn 25 In 25 precipitates that are embedded in a tetragonal AF Ni 50 Mn 50 matrix. During the annealing treatment, the spins at the interface with the AF matrix align parallel to the field direction. Then, on removal of the magnetic field, due to the magnetic proximity effect, the interfacial spins remain strongly ferromagnetically pinned along their original direction (i.e. along the magnetic field direction applied during the annealing), forming the shell ferromagnet structure. Furthermore, X-ray diffraction analysis revealed that the size of the precipitates is strongly influenced by the annealing temperature and the annealing time (Dincklage et al., 2018).
Note that in all of the above-described work the evidence for shell ferromagnetism was obtained rather indirectly on the basis of magnetization and X-ray diffraction measurements. A key challenge in this field remains therefore the determination of the structural and magnetic properties of the nanoprecipitates generated by the segregation process using a more direct approach (e.g. via Lorentz transmission electron microscopy or small-angle X-ray or neutron scattering). Very recently, polarized small-angle neutron scattering (SANS) analysis of field-annealed off-stoichiometric Ni 50 Mn 45 In 5 Heusler alloys has suggested the presence of FM nanoprecipitates of $55 nm size surrounded by a magnetically inhomogeneous region with a size of about 20 nm (Benacchio et al., 2019).
The purpose of the present work is to clarify the magnetic microstructure of a zero-field-annealed off-stoichiometric Ni 50 Mn 45 In 5 Heusler compound. In particular, we study the magnetic field and temperature dependence of the magnetic properties using DC magnetization measurements combined with magnetic-field-dependent unpolarized SANS. Magnetic SANS appears to be well suited to obtaining bulk-averaged information on the structural and magnetic microstructure of off-stoichiometric martensitic Heusler alloys since it provides information about the perturbation of the magnetization vector field on a mesoscopic length scale of about 1-300 nm. For instance, for these types of system, magnetic SANS has been successfully employed to disclose the interplay between the nuclear and magnetic microstructure (Runov et al., 2001(Runov et al., , 2003(Runov et al., , 2004(Runov et al., , 2006 and to reveal the presence of nanometresized spin clusters in martensitic Ni-Mn-based Heusler alloys (Bhatti et al., 2012;El-Khatib et al., 2019;Sarkar et al., 2020). The paper is organized as follows. Section 2 provides some details about the sample synthesis process, the sample characterization and the neutron experiment. Section 3 gives a brief overview of the main expression for the unpolarized magnetic SANS cross section and describes the different neutron data analysis procedures to determine the purely magnetic SANS cross section and the underlying magnetic correlation function. Section 4 presents and discusses the experimental results, while Section 5 summarizes the main findings of this study. Appendix A displays the experimental 2D total (nuclear + magnetic) SANS cross sections from which the 1D SANS cross sections have been determined. Appendix B provides additional information on the procedure employed to estimate the nuclear scattering contribution. Finally, Appendix C summarizes the 1D total (nuclear + magnetic) SANS cross sections, the purely magnetic SANS cross sections, and the computed magnetic distance distribution functions.

Experimental
The synthesis procedure for the preparation of the offstoichiometric Ni 50 Mn 45 In 5 polycrystalline alloy (nominal composition) used in this study is similar to that described by Benacchio et al. (2019). It consists of a three-step process: (i) the sample was prepared by arc-melting from high-purity elements (99.9%), followed by (ii) annealing under an Ar atmosphere at 1073 K in a sealed quartz tube for 5 days (and then quenching in water at room temperature), and finally (iii) the specimen was post-annealed in zero applied magnetic field at 700 K for 12 h, which is expected to result in an equilibrium microstructure. The thickness of the sample was estimated to be $0.585 mm and the sample's surface area was determined as $0.248 cm 2 .
The structural properties were determined by wide-angle X-ray diffraction (XRD) using a Bruker D8 DISCOVER diffractometer in Bragg-Brentano geometry (Cu K radiation).  A sketch of the magnetic SANS setup. The momentum transfer vector q corresponds to the difference between the wavevectors of the incident (k 0 ) and scattered (k 1 ) neutrons, i.e. q = k 0 À k 1 . The magnetic field H 0 is applied perpendicular to the incident neutron beam, i.e. H 0 k e z ? k 0 . For small-angle scattering, i.e. É ( 1, the component q x of q is smaller than the other two components q y and q z , so that only correlations in the plane perpendicular to the incident neutron beam are probed. Magnetization measurements were performed using a Cryogenic Ltd vibrating sample magnetometer equipped with a 14 T superconducting magnet. The neutron measurements were conducted at the ZOOM instrument at the ISIS neutron and muon source (United Kingdom). Fig. 1 depicts the experimental SANS setup used for this study. The measurements were done in time-of-flight mode using a white incident neutron beam. The neutron experiments were conducted at selected temperatures of 280, 250, 200, 150, 50 and 10 K and within a q range of about 0.04 q 0.90 nm À1 [q = (4/) sin(É/2), where É is the scattering angle and is the wavelength of the incident radiation]. A magnetic field H 0 was applied perpendicular to the incident neutron beam ðH 0 k e z ? k 0 Þ. The neutron data at each selected temperature were recorded by reducing the magnetic field from 7 T (maximum field available) down to 0 T following the magnetization curves (see Fig. 3). The neutron data reduction (corrections for background scattering and transmission) was carried out using the standard procedure implemented in the Mantid software (Arnold et al., 2014).

Unpolarized SANS cross section
For the scattering geometry where the magnetic field H 0 is applied perpendicular to the incident neutron beam (see Fig. 1), the elastic unpolarized total (nuclear + magnetic) SANS cross section dAE/d at momentum-transfer vector q can be written as (Michels, 2021) where V is the scattering volume, b H = 2.91 Â 10 8 A À1 m À1 relates the atomic magnetic moment to the atomic magnetic scattering length,Ñ NðqÞ andM MðqÞ ¼ fM M x ðqÞ;M M y ðqÞ;M M z ðqÞg represent the Fourier transforms of the nuclear scattering length density N(r) and of the magnetization vector field M(r) = {M x (r), M y (r), M z (r)}, respectively, specifies the angle between H 0 and q ' q{0, sin(), cos()} in the small-angle approximation, and the asterisks * denote the complex conjugated quantities. Equation (1) shows that for a fully saturated material (M x = M y = 0) the SANS signal (in the perpendicular scattering geometry) exhibits the well known sin 2 () anisotropy, provided that there exists a contrast in the longitudinal magnetization component M z (r) on the length scale probed by SANS. Away from saturation, more complicated angular anisotropies may be expected due to the contribution of the transverse magnetization Fourier components.
In our neutron data analysis below, we subtracted the azimuthally averaged (over AE10 ) 1D SANS cross section along the field direction (q || H 0 ) and at the largest available field of 7 T (approach-to-saturation regime; compare Fig. 3) from the azimuthally averaged (over 2 radians) 1D SANS cross section measured at lower fields. 21 This subtraction procedure eliminates the (field-independent) nuclear SANS contribution / jÑ Nj 2 and yields the following 1D purely magnetic SANS cross section dAE mag /d, where the Á stand for the differences between the Fourier components at the two fields considered (low-field data minus the 7 T data). We emphasize that dAE mag /d is strongly dominated by the two transverse magnetization Fourier componentsM M x;y .

Magnetic correlation function
Generally, for a ferromagnetic material the magnetic correlation function reflects the spatial variation (perturbation) of the perpendicular magnetization components around microstructural defects (such as the precipitates studied here). Increasing the applied field results in the suppression of the amplitude and of the range of the spin-misalignment correlations around the defect. In this study, the real-space 1D magnetic distance distribution function P mag (r) = r 2 C mag (r), with C mag (r) being the magnetic correlation function, has been computed numerically from the experimental 1D purely magnetic SANS cross section dAE mag /d via an indirect Fourier transform (IFT) (Glatter, 1977). In this case, the N-dimensional vector P mag (r) is determined by minimizing the function where = (q) is the standard deviation of each data point, A is the data transfer matrix, which in the case of 1D IFT has the elements A ij = 4[sin(q i r j )/q i r j ]Ár j , and L is a regularization matrix that is multiplied by the regularization parameter . The numerical inversion method has already been used successfully in several other studies, e.g. to investigate the structural and magnetic properties of nanoparticles (Bender, Balceris et al., 2017;Bender, Bogart et al., 2017) and to extract the underlying 2D magnetic correlations in a nanocrystalline bulk ferromagnet (Bender et al., 2021). The full Python script used to perform the IFT and extract the 1D correlation function from the 1D SANS data can be found on the Github repository (https://github.com/ PBenderLux/Data-analysis). research papers 4. Results and discussion Fig. 2 presents the wide-angle XRD results for the Ni 50 Mn 45 In 5 alloy. The XRD pattern features broad reflections, which can be ascribed to two crystallographic phases: the tetragonal antiferromagnetic Ni 50 Mn 50 phase (I4/mmm, a ' 2.64 Å , c ' 3.50 Å ) with an average crystallite size of about 50 nm, and the initial tetragonal Ni 50 Mn 45 In 5 phase (I4/mmm, a ' 3.77 Å , c ' 7.0 Å ) with an estimated particle size of 8 nm. As discussed in the Introduction, these findings suggest that the phase separation at 700 K is not fully completed after 12 h of annealing and some initial phase remains intact, in agreement with the results of Ç akır et al. (2016) and Dincklage et al. (2018). However, in contrast to the previous studies, the cubic Ni 50 Mn 25 In 25 phase (i.e. the Heusler nanoprecipitates) cannot be detected in the XRD pattern. As discussed by Benacchio et al. (2019), a possible explanation for this could be the presence of a few large grains and/or a strongly bimodal particle-size distribution in the sample, which could prevent the detection of small quantities of nanoprecipitates by XRD. Note that the lattice parameter values obtained using the Le Bail fit (LBF) method for the tetragonal Ni 50 Mn 50 phase are in line with the ones reported in the International Centre for Diffraction Data (ICDD; http://www.icdd.com) database . No record could be found in the ICDD database for the initial Ni 50 Mn 45 In 5 phase. Further complementary structural characterization methods, such as electron microscopy or neutron diffraction (as a function of annealing time and temperature), are required to obtain additional information on the microstructure of the zero-field-annealed Ni 50 Mn 45 In 5 alloy, in particular regarding here the observed absence of the cubic Ni 50 Mn 25 In 25 phase. Fig. 3 displays the magnetization curves of the Ni 50 Mn 45 In 5 alloy at different temperatures. The magnetization does not saturate even at the highest applied magnetic field values, and exhibits a hysteresis with a coercive field that increases with decreasing temperature from 46 mT at 280 K to 88 mT at 10 K (see inset in Fig. 3). The presence of both features points to the coexistence of a paramagnetic-like and ferromagnetic contribution, respectively. As previously reported (Ç akır et al., 2016, 2017), the emergence of a ferromagnetic-like behaviour in Ni 50 Mn 45 In 5 strongly suggests the formation of dominantly ferromagnetic nanoprecipitates in an AF Ni-Mn matrix. From the estimated saturation magnetization at 10 K [M S = 11.1 A m 2 kg À1 , determined from a linear fit of M(1/H 0 ) for high field values] and the specific magnetization analysis detailed by Ç akır et al. (2016), we estimate that about 60% of the Ni 50 Mn 45 In 5 sample has been decomposed into Ni 50 Mn 25 In 25 . This result therefore supports the hypothesis of an incomplete phase separation process, as already suggested by the XRD results. Moreover, the absence of a vertical shift in the magnetization curves (found in the field-annealed samples) indicates the (expected) absence of interfacial spin ordering between the AF matrix and the FM nanoprecipitates during nucleation and growth, as has been already discussed by Ç akır et al. (2016,2017). Fig. 4(a) shows the magnetic field dependence of the azimuthally averaged (over 2 radians) total (nuclear + magnetic) SANS cross section dAE/d at the selected temperature of 280 K. The cross section dAE/d exhibits a  XRD pattern for Ni 50 Mn 45 In 5 alloy (Cu K radiation) (black crosses). The red dashed line shows the XRD data refinement using the Le Bail fit (LBF) method implemented in the FULLPROF software (Rodríguez-Carvajal, 1993) and considering two tetragonal phases in the space group I4/mmm. The bottom blue solid line represents the difference between the calculated and experimental intensities.   broad shoulder at intermediate momentum transfers q and a weakly magnetic field dependent intensity at the smallest q. Since the nuclear scattering is field independent, the magnetic field dependence of dAE/d can only result from the magnetic scattering. Fig. 4(b) presents the corresponding purely magnetic SANS cross section dAE mag /d, which was obtained using the specific neutron data procedure developed in Section 3.1. The strong field dependence of dAE mag /d at small q is due to spin-misalignment scattering, i.e. it results from the failure of the spins to be completely aligned along H 0 . In this way (via the subtraction procedure), the broad shoulder at intermediate q and the magnetic field dependence of the SANS signal at the smallest q become more clearly visible. These particular magnetic features, in addition to the sin 2 ()type angular anisotropy due to longitudinal magnetization fluctuations [compare equation (1)] observed in the 2D SANS patterns (see Appendix A), were also observed in fieldannealed Ni 50 Mn 45 In 5 samples. The origin of these three features in the SANS signal has been attributed to the formation of annealing-induced ferromagnetic nanoprecipitates in the AF matrix (Benacchio et al., 2019). More specifically, the particles represent a source of perturbation, which gives rise to canted spin moments in the surroundings of the particle-matrix interface, e.g. via inhomogeneous dipolar stray fields and/or strain fields that are related to the jump in the magnetization in the vicinity of the particle-matrix interface. Fig. 5(a) presents the magnetic field dependence of the numerically computed magnetic distance distribution function P mag at 280 K. The P mag profiles are strongly affected by the applied magnetic field strength. In particular, by reducing the magnetic field, we see that (i) the oscillatory behaviour with negative P mag values vanishes, and (ii) the zero crossings shift to larger r values. As previously discussed (Benacchio et al., 2019), here the origin of the negative part of the oscillatory P mag may be attributed to the spatial nanometre-scale variation in the orientation of the magnetic moments around the annealing-induced ferromagnetic nanoprecipitates, rather than to an inhomogeneous core-shell-type structure (Lang & Glatter, 1996). More precisely, for a dipolar-type perturbation such as the one sketched in Fig. 6(a), the transverse magnetization components (M x , M y ) change their sign in the direction of the applied field, in this way giving rise to negative values of the distance distribution function (termed anticorrelations). The zero crossings and the minima of P mag are dependent on the applied field H 0 . Fig. 5(b) depicts the corresponding correlation function C mag = P mag /r 2 . Due to the r 2 factor, features in P mag at medium and large distances are more pronounced than in C mag . In agreement with the functional behaviour of P mag (r), we see that increasing the field results in a reduction in the amplitude and range of the spinmisalignment correlations. The C mag (r) shapes agree qualitatively with the ones computed numerically by Erokhin et al. (2015) for a nanoporous dipolar stray-field-dominated system, supporting therefore the existence of anticorrelations in Ni 50 Mn 45 In 5 .
The disappearance of the oscillatory character in P mag for r > 30 nm with decreasing field can be qualitatively interpreted using the law of approach to ferromagnetic saturation for inhomogeneous spin states. Magnetization nonuniformities are induced by the stress fields of microstructural defects such as point defects, dislocations, grain boundaries or precipitates (Kronmü ller & Fä hnle, 2003). The field-dependent micromagnetic exchange length l H / H À1/2 characterizes the size of these nonuniformities and can be seen as the resolution limit of the magnetization. At applied fields of the order of a few tesla, l H takes on values of the order of a nanometre, and may increase to about 100 nm (and even larger) in small fields. At remanence, l H becomes larger than the average distance R between the magnetic nanoprecipitates, so that the nanoprecipitates act magnetically as one superdefect with a corresponding (large) magnetic correlation length that, in our (a) The field dependence of the magnetic distance distribution function P mag (r) at 280 K. The P mag (r) values were computed numerically via an indirect Fourier transform (IFT) of the experimental dAE mag /d data shown in Fig. 4(b). Note that for comparison with the results obtained at lower temperatures, as summarized in Appendix C, the P mag at each field has been normalized by the maximum peak intensity value obtained at remanence. (Inset) A comparison between the experimental dAE mag /d plotted in Fig. 4(b) (coloured open circles) and the reconstructed dAE mag / d based on the IFT of the numerically computed P mag shown in Fig. 5(a) (coloured solid lines). (b) The corresponding magnetic correlation function C mag (r) = P mag (r)/r 2 (semi-logarithmic sale). (a) A simplified sketch of the spin-misalignment correlations around defects in an antiferromagnetic matrix. The jump in the magnetization magnitude at the interface between the precipitate and the matrix gives rise to a dipolar stray field (drawn here with spherical symmetry for simplicity), which itself exerts a torque on the matrix spins and in this way produces spin disorder and a concomitant field-dependent contrast for magnetic SANS. R denotes the average distance between defects. Coloured arrows represent the magnetization component M ? perpendicular to H 0 . (b), (c) Illustrations of the magnetization distribution around defects for the cases of l H ) R (low field) and l H ( R (large field), respectively. Adapted from Kronmü ller & Seeger (1961). experiment, lies outside of the available experimental q range. By contrast, near saturation, l H becomes smaller than R, and the magnetization distribution then follows each individual defect (nanoprecipitate). Since their sizes are of the order of a few tens of nanometres, the correlation features in P mag become visible within the available experimental q range and for the highest field (near to saturation). Fig. 6 graphically illustrates the magnetization distribution around the nanoprecipitates (defects) at low field and at a field close to saturation. This sketch should help the reader to obtain a better understanding of the physical picture behind our discussion.
Therefore, similar to our previous work (Benacchio et al., 2019), from the P mag data computed in the highest fields, one can relate the first and second zero crossings to the size of the magnetically inhomogeneous region surrounding the nanoprecipitates and to the size D of the individual nanoprecipitates. Near saturation (  The magnetic field and temperature dependence of the experimental 2D total (nuclear + magnetic) SANS cross section dAE/d. The applied magnetic field is horizontal in the plane of the detector ðH 0 ? k 0 Þ. Note that the dAE/d are plotted in polar coordinates with q in nm À1 , in degrees and the intensity in cm À1 . and ' 30 nm. Note that both quantities and D seem to be temperature independent at 7 T (compare the P mag plots in Appendix C). The value for is slightly larger than the one determined for the 5 T field-annealed sample (Benacchio et al., 2019). This increase can be easily understood by considering the role played by the magnetic field on the spin configuration at the interface between the AF matrix and the FM nanoprecipitates during the annealing process. When the annealing is realized under a magnetic field, the spins at the interface can be pinned along the field direction due to the magnetic proximity effect, whereas they remain randomly oriented in the absence of a magnetic field. Therefore, an increase in the size of the magnetically inhomogeneous region seen by magnetic SANS is expected in the case of zero-fieldannealed off-stoichiometric Ni 50 Mn 45 In 5 Heusler alloys. Furthermore, the shift of the zero crossing to smaller r values with increasing field strength suggests that the canted spins at the interface tend to align with respect to the magnetic field H 0 (as expected).

Conclusions
We have employed X-ray diffraction, magnetometry and fielddependent unpolarized magnetic SANS to disclose the magnetic microstructure of a zero-field-annealed offstoichiometric Ni 50 Mn 45 In 5 Heusler alloy. X-ray diffraction reveals the presence of a nanoscale microstructure and indicates that the segregation process at 700 K is not fully completed after 12 h of annealing. The magnetometry data exhibit a ferromagnetic-like behaviour, which strongly suggests the formation of annealing-induced ferromagnetic nanoprecipitates in the antiferromagnetic matrix, as postulated by Ç akır et al. (2016,2017). The analysis of the fielddependent magnetic SANS data reveals a strong spin misalignment on the mesoscopic length scale caused by the annealing-induced ferromagnetic nanoprecipitates. In fact, the field-dependent analysis of the magnetic distance distribution function, obtained by an indirect Fourier transform technique, confirms that the nanoprecipitates are surrounded by a magnetically inhomogeneous region where the canted spins tend to align with respect to the magnetic field. Near magnetic saturation, the size of the spin-canted region and the size of the individual nanoprecipitates have been estimated to $30 and $75 nm, respectively. The presented neutron data analysis (in Fourier and real space) is particularly useful for studying the nanoscale magnetic inhomogeneities of bulk materials at the mesoscopic length scale. Finally, it demonstrates that unpolarized magnetic SANS might be a practicable alternative to time-consuming and low-intensity polarized neutron measurements.

APPENDIX A Two-dimensional total SANS cross sections
In this appendix, we provide the experimental 2D total (nuclear + magnetic) SANS cross sections dAE/d, from which the azimuthally averaged (over 2 radians and over AE10 ) 1D SANS cross sections have been determined.
As can be seen in Fig. 7, in the temperature range of 10-280 K and at the highest applied field of 7 T, the 2D neutron patterns are predominantly elongated perpendicular to the magnetic field direction. This particular feature is the signature of the sin 2 ()-type angular anisotropy [compare equation (1)]. At remanence, the patterns are isotropic. Since for an ideal defect-free AF the magnetization within a mesoscopic volume is zero, the magnetic scattering contrast would vanish. Therefore, the magnetic field dependence of the 2D SANS patterns strongly suggests the presence of an effectively ferromagnetic component in dAE/d, which is compatible with the formation of annealing-induced ferromagnetic precipitates in the AF matrix.

APPENDIX B Estimation of nuclear SANS cross section
The purpose of this appendix is to provide additional information about the procedure used here to estimate the nuclear SANS cross section dAE nuc /d. As detailed in Section 3.1, to separate the purely magnetic SANS cross section dAE mag /d from the total (nuclear + magnetic) dAE/d, it is necessary to determine dAE nuc /d. Fig. 8 presents the temperature dependence of the azimuthally averaged (over AE10 ) 1D total (nuclear + magnetic) SANS cross section dAE/d measured along the field direction (q || H 0 ) at the highest applied magnetic field of 7 T. The total dAE/d are only weakly temperature dependent within the experimental q range. Noting moreover that the sample is in the approach-to-saturation regime at 7 T (compare Fig. 3), we believe that the dAE/d data shown in Fig. 8 are a good approximation for the nuclear SANS cross section dAE nuc /d. We also remind the reader that the paramagnetic-like magnetization contribution related to the antiferromagnetic matrix is always present within the shown field range. The asymptotic power-law exponent n in dAE/d / q Àn was found to be weakly temperature dependent and smaller The temperature dependence of the azimuthally averaged (over AE10 ) 1D total (nuclear + magnetic) SANS cross section dAE/d measured along the field direction (q || H 0 ) and at the highest applied field value of 7 T (log-log scale). Dashed lines show the extrapolation of dAE/d / q Àn . The Porod fits were restricted to 0.25 q 0.46 nm À1 . (Inset) The temperature dependence of the asymptotic power-law exponent n. than the Porod value of n = 4 (see the inset of Fig. 8). Similar observations have also been reported in Heusler-derived multiferroic alloys (Bhatti et al., 2012). As discussed by those authors, the nature of the Porod scattering changes in such alloys and might be related to the magnetic ground state in the martensitic phase.
APPENDIX C One-dimensional SANS cross sections and magnetic distance distribution functions Fig. 9 summarizes the experimental azimuthally averaged (over 2 radians) 1D total (nuclear + magnetic) SANS cross sections dAE/d, the corresponding purely magnetic SANS cross sections dAE mag /d and the magnetic distance distribution functions P mag using the neutron data analysis detailed in Section 3.